CN101755057A - Low density steel with good stamping capability - Google Patents

Low density steel with good stamping capability Download PDF

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CN101755057A
CN101755057A CN200880016091A CN200880016091A CN101755057A CN 101755057 A CN101755057 A CN 101755057A CN 200880016091 A CN200880016091 A CN 200880016091A CN 200880016091 A CN200880016091 A CN 200880016091A CN 101755057 A CN101755057 A CN 101755057A
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sheet material
steel
rolling
steel sheets
temperature
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CN101755057B (en
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A·佩拉德
X·加拉
J-L·于里阿特
O·布阿兹
J·德里莱特
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ArcelorMittal France SA
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
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Abstract

The present invention relates to a kind of hot rolled ferrite steel sheets, this sheet material has following composition: 0.001＜C≤0.15% by weight, Mn≤1%, Si＜1.5%, 6%≤Al＜10%, 0.020%＜Ti＜0.5%, S＜0.050%, P＜0.1%, randomly, be selected from one or more following elements: Cr＜1%, Mo＜1%, Ni＜1%, Nb＜0.1%, V≤0.2%, B≤0.010%, the remainder of this composition constitutes by iron with from the unavoidable impurities of melting, with about rolling horizontal perpendicular surface on the average ferrite grain size d that measures IVLess than 100 microns.

Description

Low density steel with good stamping capability
Technical field
The present invention relates to a kind ofly have greater than the intensity of 400MPa with less than the hot rolling or the cold rolling ferritic steel sheet material of about 7.3 density, and manufacture method.
Background technology
Can be especially by making the Motor vehicles loss of weight reduce the CO that discharges by described Motor vehicles 2Amount.Can realize this loss of weight in the following way:
-raising constitutes the mechanical property of the steel of structure unit or top layer parts, or
-for given mechanical property, reduce the density of steel.
First method has become the theme of a lot of researchs, and Iron And Steel Industry has proposed to have 800MPa to the steel greater than the intensity of 1000MPa.But the density of these steel keeps approaching 7.8, i.e. the density of conventional steel.
Second method relates to the element that interpolation can reduce steel density.Thereby patent EP 1485511 discloses the steel that is added with silicon (2-10%) and aluminium (1-10%), and this steel has the ferrite microstructure and also contains the carbide phase.
But in some cases, but the high relatively silicone content of these steel may cause the problem of coating and ductility.
Also knownly contain the steel that 8% the aluminium of having an appointment adds.But when making these steel, particularly during cold rolling, may meet difficulty.When these steel of calendering, also can run into wrinkling (roping) problem.When such steel contained greater than 0.010% C, separating out of carbide phase can increase fragility.Thereby it is impossible utilizing such steel to come the manufacturing structure parts.
Summary of the invention
An object of the present invention is to provide hot rolling or cold-rolled steel sheet material, this sheet material has simultaneously:
-density less than about 7.3;
-greater than the intensity R of 400MPa m
-good deformability (particularly rolling during) and excellent anti-wrinkling property,
But-good weldability and good coating.
Another object of the present invention provides the compatible manufacture method of a kind of and conventional industrial plants.
For this purpose, a theme of the present invention is a kind of hot rolled ferrite steel sheets, its composition comprises as follows, content by weight: 0.001≤C≤0.15%, Mn≤1%, Si≤1.5%, 6%≤Al≤10%, 0.020%≤Ti≤0.5%, S≤0.050%, P≤0.1%, randomly, be selected from one or more following elements: Cr≤1%, Mo≤1%, Ni≤1%, Nb≤0.1%, V≤0.2%, B≤0.01%, the remainder of this composition constitutes by iron with from the unavoidable impurities of melting, with about rolling horizontal perpendicular surface on the average ferrite grain size d that measures IVLess than 100 microns.
Another theme of the present invention is cold rolling and annealed ferritic steel sheet material, and the steel of this sheet material has above-mentioned composition, is characterised in that its tissue is by average grain size d αThe axle ferrite that waits less than 50 microns constitutes, and the linear ratio f that also is intergranular κ precipitate is less than 30%, and this linear ratio f is defined by following formula:
Figure GPA00001045733200021
Figure GPA00001045733200022
The total length of representing the crystal boundary that contain κ precipitate relevant with the area of being considered (S),
Figure GPA00001045733200023
The total length of representing the crystal boundary relevant with the area of being considered (S).
According to a specific embodiment, this composition comprises: 0.001%≤C≤0.010%, Mn≤0.2%.
According to a preferred embodiment, this composition comprises: 0.010%＜C≤0.15%, 0.2%＜Mn≤1%.
Preferably, this composition comprises: 7.5%≤Al≤10%.
Most preferably, this composition comprises: 7.5%≤Al≤8.5%.
Dissolved carbon content is preferably less than 0.005 weight %.
According to a preferred embodiment, the intensity of this sheet material is equal to or greater than 400MPa.
Preferably, the intensity of this sheet material is equal to or greater than 600MPa.
Another theme of the present invention is a method of making the hot-rolled steel sheet material, in the method: the steel compositions according to one of above-mentioned composition is provided; Steel is cast as the work in-process form; Then described work in-process are heated to 1150 ℃ or higher temperature; Use at least two being higher than the rolling step of carrying out under 1050 ℃ the temperature then with this work in-process hot rolling, so that acquisition sheet material, wherein the draft of each step is equal to or greater than 30%, and elapsed time is equal to or greater than 10s between each rolling step and next the rolling step; Then 900 ℃ or higher temperature T FLUnder finish rolling; Cool off this sheet material then, make between 850 ℃ and 700 ℃ elapsed time t at interval pGreater than 3s, separate out to cause the κ precipitate; Then 500-700 ℃ temperature T CurlUnder this sheet material is curled.
According to a specific implementation method, directly between counterrotating roller, cast with the form of thin strip or thin slab.
Another theme of the present invention is a kind of method cold rolling and the annealed steel sheets of making, in the method: the hot-rolled steel sheet material of making according to one of aforesaid method is provided; With the draft of 30-90% that this sheet material is cold rolling then, so that obtain cold rolling sheet material; Then with speed V greater than 3 ℃/s cShould cold rolling sheet material be heated to temperature T '; Then with speed V less than 100 ℃/s RWith this sheet cools, the selection temperature T ' and speed V R, so that obtain recrystallize completely, the linear ratio f of intergranular κ precipitate and less than the dissolved carbon content of 0.005 weight % less than 30%.
Preferably, this cold rolling sheet material is heated to 750-950 ℃ temperature T '.
Manufacture method according to a specific cold rolling and annealed sheet provides the sheet material with following composition: 0.010%＜C≤0.15%; 0.2%＜Mn≤1%; Si≤1.5%; 6%≤Al≤10%; 0.020%≤Ti≤0.5%; S≤0.050%; P≤0.1%; Randomly, be selected from one or more following elements: Cr≤1%, Mo≤1%, Ni≤1%, Nb≤0.1%, V≤0.2%, B≤0.01%, the remainder of this composition constitutes by iron with from the unavoidable impurities of melting, and this cold rolling sheet material is heated to chosen temperature T ' down to avoid the dissolving of κ precipitate.
According to a kind of specific implementation method, the sheet material with above-mentioned composition is provided, this cold rolling sheet material is heated to 750-800 ℃ temperature T ' down.
Another theme of the present invention be the steel sheets made according to the steel sheets of one of above-mentioned embodiment or according to one of aforesaid method in making automotive field the top layer parts or the purposes in the structure unit.
Description of drawings
With the mode of embodiment and the description that provides with reference to accompanying drawing, will know other features and advantages of the present invention by hereinafter, in the accompanying drawings:
-Fig. 1 has schematically defined the linear ratio f of ferrite crystal boundary, exists intergranular to separate out in this crystal boundary;
-Fig. 2 shows the microstructure according to hot-rolled steel sheet material of the present invention;
-Fig. 3 is presented at the microstructure of the hot-rolled steel sheet material of making under the condition of discontented unabridged version invention;
-Fig. 4 and Fig. 5 illustrate the microstructure according to two cold rolling and annealed sheet materials of the present invention; And
-Fig. 6 has shown the microstructure of the cold rolling and annealed steel sheets of making under the condition of discontented unabridged version invention.
Embodiment
The present invention relates to steel, this steel has the low density less than about 7.3, but still keeps gratifying use properties.
The present invention be more particularly directed to a kind of manufacture method, this method is used in the separating out of the steel of the particular combinations that contains carbon, aluminium and titanium especially control intermetallic carbide, microstructure and texture.
As for the chemical constitution of steel, carbon plays an important role in the formation of microstructure and mechanical property.
According to the present invention, carbon content is 0.001%-0.15%.Be lower than at 0.001% o'clock, can not obtain significant sclerosis.When carbon content greater than 0.15% the time, but the cold-rolling property of steel is bad.
-when manganese content greater than 1% the time because this element forms the tendency of γ phase, have the risk that makes residual austenite stable at ambient temperature.Has the ferrite microstructure at ambient temperature according to steel of the present invention.According to carbon in the steel and manganese content, can use multiple ad hoc approach of the present invention:
-when carbon content is 0.001-0.010% and when manganese content is less than or equal to 0.2%, the minimum intensity R that is obtained mBe 400MPa;
-when carbon content greater than 0.010% but when being less than or equal to 0.15% and when manganese content greater than 0.2% but when being less than or equal to 1%, the minimum intensity that is obtained is 600MPa.
In above-mentioned carbon content scope, the inventor is verified, and this element is separated out and promoted remarkable sclerosis by the ferrite crystal grain refinement by carbide (TiC or κ precipitate).Be not intergranular (intergranulaire) if carbide is separated out, if or carbon not in sosoloid, then add the small loss that carbon only causes ductility.
In these compositing ranges, under all temperature in the manufacturing cycle process, promptly just in time from the casting after solidifying, this steel has ferrite matrix.
The same with aluminium, silicon is the element that allows to make the reduction of steel density.But excessive interpolation silicon (greater than 1.5%) then causes may occurring of high tack oxide compound formation and surface imperfection, causes the wettability deficiency especially in the galvanizing operation.In addition, this excessive interpolation has reduced ductility.
Aluminium is the important element among the present invention.When its content during, can not obtain enough density and reduce less than 6 weight %.When its content greater than 10% the time, have the intermetallic phase Fe that forms embrittlement 3The risk of Al and FeAl.
Aluminium content is preferably 7.5-10%.In this scope, the density of sheet material is less than about 7.1.
Aluminium content is preferably 7.5-8.5%.In this scope, obtain gratifying loss of weight and do not have ductility and reduce.
This steel also comprises the titanium of minimum (promptly 0.020%), because the separating out of TiC, titanium helps the carbon content in the sosoloid is restricted to less than 0.005 weight %.Carbon in the sosoloid has detrimental action to ductility, because it has reduced the mobility of dislocation.Separating out of excessive titanium carbide took place greater than 0.5% o'clock in titanium, and ductility reduces.
Optional boron adds (being limited to 0.010%), also helps to reduce the amount of the carbon in the sosoloid.
Sulphur content is less than 0.050%, so that any of restricted T iS separates out, this is separated out reduction ductility.
Reason for high-temperature ductility also is limited to 0.1% with phosphorus content.
Randomly, this steel can also contain by independent or bonded mode:
-content is equal to or less than 1% chromium, molybdenum or nickel.These elements provide additional solution hardening;
-can be by adding micro alloying element for example niobium and vanadium less than the amount of 0.1 weight % and 0.2 weight % respectively, so that obtain additional precipitation-hardening.
The remainder of this composition constitutes by iron with from the unavoidable impurities of melting.
According to the tissue of steel of the present invention, comprise the ferrite crystal grain of equally distributed height misorientation.The strong misorientation of adjacent intergranule has suppressed wrinkling defective.The feature of this defective is, and is local and occur ribbon prematurely in rolling direction during the cold-forming of sheet material, forms relief (relief).This phenomenon is to be caused by gathering of the recrystal grain of slight misorientation, because their same initial crystal grain before from recrystallize.The tissue of wrinkling sensitivity is characterised in that the spatial distribution of texture.
When having wrinkling, mechanical property transversely (particularly uniform elongation) and formability seriously descend.According to steel of the present invention because its favourable texture, therefore between shaping period to wrinkling insensitive.
According to one embodiment of the invention, at ambient temperature, the microstructure of this steel by average grain size less than 50 microns etc. axle ferrite matrix constitute.The main solid solution of aluminium is in this iron-based substrates.These steel contain the κ precipitate, and it is Fe 3AlC xCompound phase between ternary metal.In ferrite matrix, exist these precipitates to cause significant sclerosis.Yet the form that these κ precipitates are not able to significant intergranular precipitate exists, otherwise will have the obvious reduction of ductility.The inventor confirms that when the linear ratio of ferrite crystal boundary (wherein having the κ precipitate) was equal to or greater than 30%, ductility reduced.Provide the definition of this linear ratio f among Fig. 1.If considering its profile is L by length 1, L 2... L iThe specific die that crystal boundary limited in succession, then microscopic examination shows, it is d that this crystal grain can have length along crystal boundary 1... d iThe κ precipitate.Consider the area with statistical representativeness (S) (for example by constituting) of microstructure, provide the linear ratio of κ precipitate with expression formula f more than 50 crystal grain:
f = Σ ( s ) di Σ ( s ) Li
Figure GPA00001045733200062
The total length of representing the crystal boundary that comprise κ precipitate relevant with the area of being considered (S), and Expression is about the crystal boundary total length of the area (S) considered.
Thereby, the degree that on behalf of the ferrite crystal boundary, statement formula f covered by the κ precipitate.
According to another embodiment, ferrite crystal grain is not equiaxial, but its mean sizes d IVLess than 100 microns.Term d IVBe illustrated in and the grain-size that goes up about rolling horizontal perpendicular representative area (S) by the measurement of linear intercept method.Along carrying out this d with the vertical direction of this sheet thickness IVMeasure.On this non-equi-axed crystal form that has unit elongation on the rolling direction can for example be present in according to hot-rolled steel sheet material of the present invention.
Implementation method according to manufacturing hot rolled sheet of the present invention is as follows:
-steel that has according to composition of the present invention is provided; And
-from this steel casting work in-process.Can be by the billet form or carry out this casting with the form of slab continuously with about 200mm thickness.Can also between counterrotating steel rider, carry out this casting with the thin slab form of tens mm thick or with the form of thin strip.As what it will be appreciated that hereinafter, it is particularly advantageous taking this manufacture method of the form of thin product, because it makes it possible to more easily obtain to help realizing thin tissue of the present invention.Those skilled in the art just can determine to satisfy the casting condition of following two kinds of needs by means of its general knowledge: obtain the needs of thin equiaxed structure after the casting, and the needs that satisfy the general requirement of industry casting.
At first the work in-process with casting are heated to above 1150 ℃ temperature, so that all reach the temperature that helps the height distortion that steel stood during each rolling step in all positions.
Certainly, under the situation of direct thin cast strip or thin slab between the counterrotating roller, can directly after casting, begin to carry out these half-finished hot-rolled steps, reheat step in the middle of therefore not needing in this case from being higher than 1150 ℃.
After a large amount of tests, the inventor is verified, can avoid wrinkling problem and obtain very good malleability and good ductility by means of the manufacture method that comprises the following steps:
-by the series rooling step with this work in-process hot rolling, so that obtain sheet material.In these steps each all corresponding the product thickness realized by means of the roll that passes milling train reduce.Under industrial condition, during roughing work in-process on the strip mill, carry out these steps.Be defined as following ratio with each the relevant draft in these steps: (the work in-process thickness after the rolling step-rolling thickness before)/(thickness before rolling).According to the present invention, under being higher than 1050 ℃ temperature, carry out at least two in these steps, the draft of each all is equal to or greater than 30% among them.Ratio is greater than 30% each distortion and the timed interval t between the follow-up distortion iBe equal to or greater than 10s, so that at this timed interval t iAfter obtain recrystallize completely.The inventor is verified, and this certain conditions combination has caused the very significant refinement of hot rolling microstructure.This is because rolling temperature is higher than non-recrystallization temperature T NrAnd promoted recrystallize.
The inventor also confirms, thin initial tissue is for example directly cast the tissue that obtains afterwards, helps improving the speed of recrystallize.
-900 ℃ or higher temperature T FLUnder finish rolling so that obtain recrystallize completely;
-then, with the sheet cools that is obtained.The inventor is verified, when being cooled to 700 ℃ of institute's elapsed times t at interval from 850 ℃ pDuring greater than 3s, obtain TiC carbide and κ precipitate and especially effectively separate out.Therefore, having obtained to help hardened separates out strongly; With
-then, 500-700 ℃ temperature T CurlUnder this sheet material is curled.This step has been finished TiC and has been separated out.
Thereby acquisition has for example hot rolled sheet of 2-6mm thickness in this stage.Manufacturing has for example sheet material of 0.6-1.5mm of less thickness if desired, and then manufacture method is as follows:
-hot rolled sheet of making is provided as stated above.Certainly, if the surface smoothness of sheet material is had requirement, then carry out the pickling operation by means of known method own;
-then, carrying out cold rolling manipulation, draft is 30-90%; And
-then, with heating rate V greater than 3 ℃/s cShould heat by cold rolling sheet material, so that suppress to reduce the answer of follow-up recrystallize ability.Carry out this reheat down at annealing temperature T ', the selective annealing temperature T ', so that obtain the perfect recrystallization of the initial tissue of height work hardening.
Then, with speed V less than 100 ℃/s RWith this sheet cools, so that do not cause any embrittlement because of too much solid solution carbon.This result is unexpected especially, because originally think that fast rate of cooling will help reducing embrittlement and separate out.At present, the inventor is verified, slowly to cool off less than the rate of cooling of 100 ℃/s, causes separating out of a large amount of carbide, this thereby reduce dissolved carbon content.This is separated out has the effect that improves intensity, and not to the detrimental action of ductility.
Select this annealing temperature T ' and speed V R, so that on the finished product, obtain:
-recrystallize completely;
-the linear ratio f of κ intergranular precipitate less than 30%; And
-dissolved carbon content less than 0.005%.
Preferably, will select temperature T ' for 750-950 ℃, so that obtain perfect recrystallization.More particularly, when carbon content greater than 0.010% but when being less than or equal to 0.15% and, temperature T ' so that further be suppressed at the dissolving of the κ precipitate that exists before the annealing will be selected when manganese content but when being less than or equal to 1% greater than 0.2%.This is because if these precipitates dissolve, then the intergranular form with embrittlement takes place follow-up separating out when slowly cooling off: too high annealing temperature can cause making the κ precipitate that forms during the hot rolled sheet dissolves again, and reduces physical strength.For this purpose, preferably select temperature T ' for 750-800 ℃.
By means of non-limiting example, following result will demonstrate the advantageous property of being given by the present invention.
Embodiment 1: hot rolled sheet
Make steel in the following way: steel is cast as half-finished form with about 50mm thickness.In following table 1, provided its composition, represented with weight percentage.
Figure GPA00001045733200091
With under the temperature of this work in-process reheat to 1220 ℃ and hot rolling to obtain the sheet material of about 3.5mm thickness.
From same composition, make some steel stand multiple hot-rolled condition.Mark I1-a, I1-b, I1-c, I1-d and I1-e represent for example from form 5 steel sheets that I1 makes under different condition.
For steel I1 to I3, table 2 has been listed the condition of follow-up hot-rolled step in detail:
-N is the rolling number of steps of carrying out under 1050 ℃ the hot-rolled temperature being higher than;
-wherein, Ni be draft greater than 30% rolling number of steps;
-each N iInstitute's elapsed time is t between step and the rolling step following closely i
-rolling end temp is T FL
-when between 850 and 700 ℃ the cooling time institute's elapsed time be spaced apart t pAnd
-the temperature of curling is T Curl
Table 2: creating conditions during hot rolling
Mark ??N ??N i ??t 1(s) ?T R(℃) ??t p(s) ??T Curl(℃)
???I1a ???I ???4 ???3 ??14.5??20.6??26.8 ???900 ???21 ???700
?? I1b ??R ??6 ??2 ?? 2??? 2 ????900 ????21 ????700
?? I1c ??R ??4 ?? 1 ?? 8 ??900 ?? 1.3 ??700
???I1d ???I ???5 ???3 ??26.5??23.5??20 ???900 ???21 ???700
???? I1e ????R ????7 ????5 ?? 7.7?? 5.2?? 3.5?? 3?? 2.5 ????1050 ????20 ????700
??I3a ??I ??4 ??2 ??10??11 ??950 ??20 ??700
?? I3b ??R ??4 ?? 1 ?? 5 ??950 ??20 ??700
I=is according to the present invention; The R=reference;
Be added with the value of underscore: not according to the present invention.
Table 3 has shown density and some mechanical property and the microstructure of measuring on the sheet material of table 2.Thereby, about rolling transversely measured as follows: intensity R m, uniform elongation A uWith tension set A tAlso according to NF EN ISO 643 standards, use the linear intercept method measured with about rolling horizontal perpendicular lip-deep grain-size d IV, along carrying out d perpendicular to the direction of sheet thickness IVMeasurement.In order to obtain the enhanced mechanical property, more particularly seek grain-size d less than 100 microns IV
Table 3: the performance of the hot rolled sheet that obtains from steel I1 and I3
Mark ??R m(MPa) ??A u(％) ??A t(％) Density ??D IV
??I1a ??I ??505 ??10.7 ??25.4 ??7.05 ??75
?? I1b ??R ??507 ??n.d ??n.d ??7.05 ?? 200
?? I1c ??R ??474 ??n.d ??n.d ??7.05 ?? 450
??I1d ??I ??524 ??n.d ??n.d ??7.05 ??40
?? I1e ??R ??504 ??n.d ??n.d ??7.05 ?? 120
??I3a ??I ??645 ??n.d ??n.d ??7.07 ??70
?? I3b ??R ??628 ??n.d ??n.d ??7.07 ?? 400
I=is according to the present invention; The R=reference;
The n.d=undetermined; Be added with the value of underscore: not according to the present invention.
Be characterised in that according to steel sheets of the present invention (in Fig. 2, having shown its microstructure), less than 100 microns grain-size d about sheet material I1d IV, and have the physical strength of 505-645MPa.
With time rolled sheet I1b and I1e between too short passage.Thereby its tissue is thick, and is non-recrystallize or insufficient recrystallize, as relates to the shown in Figure 3 of sheet material I1e.Therefore, ductility reduces, and this sheet material is responsive to wrinkling defective.Can draw similar conclusion for sheet material I3b.
With the rolling step of number deficiency, draft, time and too short timed interval t between too short passage greater than 30% p, I1c is rolling with sheet material.These results with noticed about sheet material I1b and I1e those come to the same thing.Because timed interval t pToo short, the sclerosis that κ precipitate and carbide TiC only partly take place is separated out, and can not make full use of the hardened possibility thus.
To be rolled from the work in-process that reference steel R1-R6 makes, so that under create conditions identical, make hot rolled sheet with the I3a steel of table 2.In table 4, provided the performance that on these sheet materials, obtains.
Table 4: the mechanical property of the hot rolled sheet that obtains from steel R1-R6.
Mark ??R e(MPa) ??R m(MPa) ??A u(％) ??A t(％) Density
??R1 ??n.d ??n.d ??n.d ??n.d ??7.2
??R2 ??n.d ??n.d ??n.d ??n.d ?? 7.44
??R3 ??n.d ??450 ?? 0.1 ?? 0.1 ??6.48
??R4 ??725 ??786 ?? 0.6 ?? 0.6 ??6.67
??R5 ??596 ??687 ?? 2.7 ?? 2.7 ??6.9
??R6 ??853 ??891 ?? 0.7 ?? 0.7 ??6.7
I=is according to the present invention; The R=reference;
The n.d=undetermined; Be added with the value of underscore: not according to the present invention.
Steel R1 has insufficient titanium content, causes too high dissolved carbon content thus, thereby flexible reduces.
Steel R2 has insufficient aluminium content, hinders the density that obtains less than 7.3 thus.
Steel R3, R4, R5 and R6 contain too high aluminium content and possible carbon.Because intermetallic compound phase or the excessive of carbide are separated out, their ductility reduces.
Embodiment 2: cold rolling and annealed sheet material
From hot-rolled steel sheet material I1a and I3-a (according to the present invention) and I1-c and I-3b (condition of discontented unabridged version invention), the draft with 75% carries out cold rolling manipulation, so that obtain the sheet material of the about 0.9mm of thickness.But during this step, demonstrate cold-rolling property.Then carry out annealing operation, it is characterized in that heating rate V c=10 ℃/s.Annealing temperature T ' and rate of cooling V in table 5, have been provided RUnder these conditions, this annealing causes recrystallize completely.
From same hot rolled sheet, make some steel carry out various cold rolling and annealing conditions.Mark I3a1, I3a2, I3a3, I3a4 for example represent four steel sheets making from hot rolled sheet 13a under different cold rolling and annealing conditions.
Table 5: the creating conditions of cold rolling and annealed sheet
Mark But cold-rolling property ??T′ ??V R
??I1a1 ??I Satisfied ??900℃ ??13℃/s
??I1a2 ??R Satisfied ??900℃ ?? 150℃/s
?? I1c1 ??R Satisfied ??900℃ ??13℃/s
??I3a1 ??I Satisfied ??800℃ ??13℃/s
?? I3a2 ??R Satisfied ??800℃ ?? 150℃/s
?? I3a3 ??R Satisfied ?? 900℃ ??13℃/s
Mark But cold-rolling property ??T′ ??V R
?? I3a4 ??R Satisfied ?? 900℃ ?? 150℃/s
?? I3b ??R ?? Dissatisfied(cracking in the horizontal)
I=is according to the present invention; The R=reference; Be added with the value of underscore: not according to the present invention.
Table 6 has shown some mechanical property, chemical property, microstructure and the density of sheet material in the table 5.Thereby, by measuring yield strength R about the rolling tension test of transversely carrying out e, tensile strength R m, uniform elongation A uWith tension set A tBy sem observation, disclosed on the test sample surface of fracture that cleavage is faceted may to be existed.
Also measured the carbon content C in the sosoloid Sol, and flexible and malleability.Also disclosed the distortion after may exist wrinkling.
The microstructure of these recrystallize sheet materials by etc. the axle ferrite constitute, about rolling its average grain size d that transversely measured αAlso by means of Aphelion TMImage analysis software has been measured the degree f that the ferrite crystal boundary is covered by the κ precipitate.
Figure GPA00001045733200141
Steel sheets I1a1 and I3a1 have dissolved carbon content, equiaxed ferritic grain size and the crystal boundary level of coverage f that satisfies condition of the present invention.Therefore, the flexible of these sheet materials, malleability and anti-wrinkling property are high.
Fig. 4 illustrates the microstructure according to steel sheets I1a1 of the present invention.
Fig. 5 illustrates the microstructure according to another steel sheets I3a1 of the present invention: demonstrate the existence of κ precipitate, it only has on a small quantity and exists with the intergranular form, can keep high ductibility thus.
By contrast, with too high speed steel sheets I1a2 is cooled off after annealing: at this moment carbon in sosoloid, causes matrix ductility to reduce fully, as the part existence of brittle zone on the fracture surface.Equally, with sheet material I3a2 cooling, also cause the too much content in the sosoloid with too high speed.
Fig. 6 illustrates the microstructure at the following annealed sheet material of excessive temperature T ' I3a3: the κ precipitate dissolving that exists before the annealing, and when cooling with the intergranular form separating out subsequently of they taken place excessively.This causes the part to have brittle zone on fracture surface.
Also sheet material I3a4 is annealed causing under the partly soluble temperature of κ precipitate.Carbon content in the sosoloid is too high.
Make steel sheets I1c1 from hot rolled sheet under the condition of discontented unabridged version invention: equi-axed crystal is oversize, anti-wrinkling property and malleability deficiency.
The hot rolled sheet I 3b of discontented unabridged version invention criterion can not be out of shape, because transverse crack occurs during cold rolling.
Weld (welding two sheet materials) with homogeneous, or (weld with the steel sheets of gap-free atom: 0.002%C with following component with heterogeneous welding with same composition; 0.01%Si; 0.15%Mn; 0.04%Al; 0.015%Nb; And 0.026%Ti, represent with weight percentage), on steel sheets I1al, carried out the resistance spot welding test.Check to welding joint shows that they are flawless.
Under the situation of welding joint subsequent heat treatment, 0.096% Ti adds the carbon that has guaranteed not exist solid solution in the heat affected zone.
Steel according to the present invention demonstrate good continuously can zinc-plated property, particularly to be higher than-20 ℃ dew-point temperature, in 800 ℃ annealing cycle process.
Therefore, steel according to the present invention has particularly advantageous performance combination (but density, physical strength, deformability, weldability coating).These steel sheets can be advantageously used in automotive field makes top layer parts or structure unit.

Claims (16)

1. hot rolled ferrite steel sheets, its steel form comprise as follows, content by weight:
0.001≤C≤0.15％
Mn≤1％
Si≤1.5％
6％≤Al≤10％
0.020％≤Ti≤0.5％
S≤0.050％
P≤0.1％
Randomly, be selected from one or more following elements:
Cr≤1％
Mo≤1％
Ni≤1％
Nb≤0.1％
V≤0.2％，
B≤0.010％
The remainder of this composition constitutes by iron with from the unavoidable impurities of melting, with about rolling horizontal perpendicular surface on the average ferrite grain size d that measures IVLess than 100 microns.
2. cold rolling and annealed ferritic steel sheet material, the steel of this sheet material has the composition according to claim 1, it is characterized in that its tissue is by average grain size d αThe axle ferrite that waits less than 50 microns constitutes, and the linear ratio f that also is intergranular κ precipitate is less than 30%, and described linear ratio f is defined by following formula:
f = Σ ( s ) di Σ ( s ) Li
Figure FPA00001045733100012
The total length of representing the crystal boundary that contain κ precipitate relevant with the area of being considered (S), and
Figure FPA00001045733100013
Represent the crystal boundary total length relevant with the area of being considered (S).
3. according to the steel sheets of claim 1 or 2, it is characterized in that its composition comprises as follows, content by weight:
0.001％≤C≤0.010％
Mn≤0.2％。
4. according to the steel sheets of claim 1 or 2, it is characterized in that its composition comprises as follows, content by weight:
0.010％＜C≤0.15％
0.2％＜Mn≤1％。
5. according to each steel sheets in the claim 1 to 4, it is characterized in that its composition comprises as follows, content by weight:
7.5％≤Al≤10％。
6. according to each steel sheets in the claim 1 to 4, it is characterized in that its composition comprises as follows, content by weight:
7.5％≤Al≤8.5％。
7. according to each steel sheets in the claim 1 to 6, it is characterized in that the carbon content in the sosoloid is less than 0.005 weight %.
8. according to each steel sheets in the claim 1 to 7, it is characterized in that its intensity Rm is equal to or greater than 400MPa.
9. according to the steel sheets of claim 4, it is characterized in that its intensity Rm is equal to or greater than 600MPa.
10. the manufacture method of hot-rolled steel sheet material, in the method:
-steel that has according to each composition among the claim 1-6 is provided;
-cast described steel with the work in-process form; Then
-described work in-process are heated to 1150 ℃ or higher temperature; Then
-use at least two being higher than the rolling step of carrying out under 1050 ℃ the temperature with this work in-process hot rolling, so that acquisition sheet material, the draft of each is equal to or greater than 30% in described at least two steps, and elapsed time is equal to or greater than 10s between each and next the rolling step in described at least two rolling steps; Then
-900 ℃ or higher temperature T FLUnder finish rolling; Then
-cool off described sheet material, make between 850 ℃ and 700 ℃ elapsed time t at interval pGreater than 3s, separate out so that cause the κ precipitate; Then
-500-700 ℃ temperature T CurlDown described sheet material is curled.
11. the manufacture method according to the hot rolled sheet of claim 10 is characterized in that, directly carries out described casting with thin strip or thin slab form between counterrotating roller.
12. manufacture method cold rolling and the annealed steel sheets, in the method:
-provide according to claim 10 or the 11 hot-rolled steel sheet materials of making; Then
-with the draft of 30-90% that described sheet material is cold rolling, so that obtain cold rolling sheet material; Then
-with speed V greater than 3 ℃/s cWith described cold rolling sheet material be heated to temperature T '; Then
-with speed V less than 100 ℃/s RWith described sheet cools,
-select described temperature T ' and described speed V R, so that obtain recrystallize completely, the linear ratio f of intergranular κ precipitate is less than 30%, and the carbon content in the sosoloid is less than 0.005 weight %.
13. the manufacture method according to claim 12 is characterized in that, with described cold rolling sheet material be heated to 750-950 ℃ of temperature T '.
14. according to the manufacture method of claim 12, it is characterized in that providing the sheet material that has according to the composition of claim 4, thereby and it is characterized in that described cold rolling sheet material is heated to the dissolving of selected temperature T ' inhibition κ precipitate.
15. according to the manufacture method of claim 12, it is characterized in that providing the sheet material that has according to the composition of claim 4, and it is characterized in that with described cold rolling sheet material be heated to 750-800 ℃ temperature T '.
16. according in the claim 1 to 9 each steel sheets or according to the steel sheets of each manufacturing in the claim 10 to 15, in automotive field in order to make the purposes of top layer parts or structure unit.
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